WO2020184162A1

WO2020184162A1 - Thick steel sheet and production method therefor

Info

Publication number: WO2020184162A1
Application number: PCT/JP2020/007377
Authority: WO
Inventors: 佐藤　祐也; 茂樹木津谷; 周作太田; 横田　智之
Original assignee: Ｊｆｅスチール株式会社
Priority date: 2019-03-13
Filing date: 2020-02-25
Publication date: 2020-09-17
Also published as: EP3916112A4; KR102586482B1; US20220154303A1; EP3916112B1; JPWO2020184162A1; JP7067628B2; EP3916112A1; CN113631731A; KR20210125057A

Abstract

The purpose of the present invention is to provide a thick steel sheet having excellent deformation characteristics at a center portion in the thickness direction thereof; and a production method therefor. This thick steel sheet is characterized by having a component composition containing, in mass%, 0.01-0.15% of C, 0.01-1.00% of Si, 0.10-2.00% of Mn, 0.010% or less of P, 0.0050% or less of S, 0.002-0.100% of Al, 5.0-10.0% of Ni, and 0.0010-0.0080% of N, the balance being Fe and incidental impurities, and having a tensile reduction of area of 30% or more in the thickness direction thereof at a center portion thereof in the thickness direction.

Description

Thick steel plate and its manufacturing method

The present invention relates to a thick steel plate suitable for structural steel used in an extremely low temperature environment such as a tank for a liquefied gas storage tank, and a method for manufacturing the same. In particular, the present invention relates to a thick steel sheet having excellent mechanical properties at the center of the sheet thickness, particularly excellent deformation characteristics, and a method for manufacturing the same. The thick steel plate in the present invention refers to a steel plate having a thickness of 6 to 80 mm.

Thick steel sheets used in extremely low temperature environments such as tanks for liquefied gas storage tanks are required to have not only the strength of the steel sheet but also the toughness at extremely low temperatures. For example, when a thick steel plate is used for a storage tank of liquefied natural gas (LNG), it is necessary to secure excellent toughness at -164 ° C. or lower, which is the boiling point of LNG. If the low temperature toughness of the steel material is inferior, the safety of the structure for the cryogenic storage tank may not be maintained. Therefore, there is a strong demand for improved low temperature toughness for the applied thick steel sheet. In response to such demands, Ni-containing thick steel sheets such as 7% Ni steel sheets and 9% Ni steel sheets having a retained austenite structure that does not show brittleness at extremely low temperatures are used.

In order to obtain excellent low-temperature toughness, Patent Document 1 discloses a method of refining untransformed austenite and lowering the Mf point by introducing lattice defects to stabilize a retained austenite structure that tends to become unstable at low temperature. ing. Further, in Patent Document 2, by adjusting Si, Al and N, and by controlling the Fe content in the residue after the reproduction heat cycle test, the CTD characteristics of the weld heat affected zone including the weld toe end are controlled. An excellent ultra-low temperature steel is disclosed. Further, Patent Document 3 discloses a thick steel sheet having excellent yield safety, tensile strength, and toughness value at a predetermined value or more at an extremely low temperature, and a method for manufacturing the same.

International Publication No. 2007/034576 International Publication No. 2007/080646 Japanese Unexamined Patent Publication No. 2011-241419

For example, in a structure for a cryogenic storage tank used in a cryogenic environment, a T-shaped joint is formed around the joint between the bottom plate and the side plate. As the size of the tank increases, the stress acting on the steel material increases, and from the viewpoint of safety, the steel material is required to have deformation performance in the plate thickness direction. Therefore, it is required to secure the deformation characteristics of the central portion of the plate thickness, which tends to be inferior in characteristics.

However, with respect to conventional Ni-containing thick steel sheets such as Patent Documents 1 to 3, attention has not been paid to the deformation characteristics of the central portion of the plate thickness, and it cannot be said that the deformation characteristics of the central portion of the plate thickness are sufficiently secured. ..

The present invention has been made in view of the above problems, and an object of the present invention is to provide a thick steel sheet having excellent deformation characteristics at the center of the plate thickness and a method for manufacturing the same.

In order to achieve the above problems, the present inventors have conducted intensive research on the composition of steel sheets and the manufacturing method for thick steel sheets containing Ni, which are suitable for structural steels used in an extremely low temperature environment. The following findings were obtained.
1. 1. By controlling the drawing value due to the tension in the plate thickness direction at the plate thickness center portion, the deformation performance of the plate thickness center portion can be improved.
2. 2. In the finish rolling of the hot rolling process, rolling with a rolling shape ratio of 0.7 or more per pass for at least 2 of the final 3 passes with a rolling reduction ratio of 3 or more causes casting defects and the center of the plate thickness. It is possible to suppress the coarse grain in the sheet and to sizing the entire steel sheet, and to improve the tensile property (rolling value) in the plate thickness direction at the center of the plate thickness.
3. 3. In the tensile characteristics (drawing value) in the plate thickness direction at the center of the plate thickness, the more casting defects existing in the center of the plate thickness and the coarse MnS having a major axis of 100 μm or more, the lower the drawing value. Further, the more coarse old austenite grains having a diameter equivalent to a circle of 100 μm or more are present, the lower the drawing value is. This is because stress concentration occurs in casting defects, coarse MnS and coarse old austenite grains, which is a starting point of fracture.
4. By controlling the S content to 0.0050% or less and reducing central segregation under light pressure during continuous casting, casting defects and coarse MnS are reduced, and tensile characteristics in the plate thickness direction (drawing value) at the center of the plate thickness. ) Can be further improved.

The present invention has been made by further studying the above findings, and the gist thereof is as follows.
[1] In terms of mass%, C: 0.01 to 0.15%, Si: 0.01 to 1.00%, Mn: 0.10 to 2.00%, P: 0.010% or less, S: It contains 0.0050% or less, Al: 0.002 to 0.100%, Ni: 5.0 to 10.0%, N: 0.0010 to 0.0080%, and consists of the balance Fe and unavoidable impurities. A thick steel sheet having a component composition and having a drawing value of 30% or more due to tension in the plate thickness direction at the center of the plate thickness.
[2] Further, in mass%, Cr: 0.01 to 1.50%, Mo: 0.03 to 1.0%, Nb: 0.001 to 0.030%, V: 0.01 to 0.10. %, Ti: 0.003 to 0.050%, B: 0.0003 to 0.0100%, Cu: 0.01 to 1.00%, and contains one or more selected from [1]. The thick steel plate described in.
[3] Further, in terms of mass%, Sn: 0.01 to 0.30%, Sb: 0.01 to 0.30%, W: more than 0 to 2.00%, Co: more than 0 to 2.00%, One selected from Ca: 0.0005 to 0.0050%, Mg: 0.0005 to 0.0050%, Zr: 0.0005 to 0.0050%, REM: 0.0010 to 0.0100% or The thick steel plate according to [1] or [2], which contains two or more kinds.
[4] A slab having the component composition according to any one of [1] to [3] is heated to 1000 ° C. or higher and 1300 ° C. or lower, and then rolled at a reduction ratio of 3 or more and at least one of the final 3 passes. A method for manufacturing a thick steel sheet by hot rolling in which the rolling shape ratio per pass is 0.7 or more for 2 passes.

According to the present invention, a thick steel plate having excellent deformation characteristics at the center of the plate thickness can be obtained. The thick steel plate of the present invention greatly contributes to improving the safety of steel structures used in extremely low temperature environments such as tanks for liquefied gas storage tanks, and brings about a remarkable industrial effect.

An embodiment of the present invention will be described below. The present invention is not limited to the following embodiments.

First, the component composition of the steel sheet of the present invention and the reason for its limitation will be described. In addition,% representing a component composition shall mean mass% unless otherwise specified.

C: 0.01-0.15%
C is effective for increasing the strength, and in order to obtain the effect, C needs to be contained in an amount of 0.01% or more. It is preferably 0.03% or more. On the other hand, if it is contained in excess of 0.15%, it segregates in the center of the plate thickness and promotes excessive precipitation of Cr carbides and Nb, V, Ti-based carbides, so that the low temperature toughness is lowered and the drawing value is lowered. .. Therefore, C is set to 0.15% or less. It is preferably 0.10% or less.

Si: 0.01-1.00%
Si is not only necessary in the steelmaking process because it acts as a deoxidizing agent, but also has the effect of increasing the strength of the steel sheet by solid solution strengthening by solid solution in steel. In order to obtain such an effect, Si needs to have a content of 0.01% or more. On the other hand, if it is contained in excess of 1.00%, the weldability and surface properties are deteriorated. Therefore, Si is set to 1.00% or less. It is preferably 0.5% or less. More preferably, it is 0.3% or less.

Mn: 0.10 to 2.00%
Mn is an element that enhances the hardenability of steel sheets and is effective in increasing the strength. In order to obtain this effect, Mn needs to be contained in an amount of 0.10% or more. Preferably, it is 0.40% or more. On the other hand, when the content exceeds 2.00%, the center segregation is promoted, which causes a decrease in cryogenic toughness, deterioration of the drawing value due to tension in the plate thickness direction at the center of the plate thickness, and occurrence of stress corrosion cracking. Further, in the central portion of the plate thickness, the generation of coarse MnS having a major axis of 100 μm or more, which is the starting point of fracture, is promoted, and the drawing value due to tension in the plate thickness direction is significantly deteriorated. Therefore, Mn is set to 2.00% or less. Preferably, it is 1.00% or less.

P: 0.010% or less When P is contained in excess of 0.010%, it segregates at the grain boundaries and lowers the grain boundary strength, which becomes a fracture starting point. As a result, drawing by tension in the plate thickness direction at the center of the plate thickness. The value drops. Therefore, it is desirable to reduce P as much as possible, and P is 0.010% or less.

S: 0.0050% or less S forms MnS in steel and significantly deteriorates low temperature toughness and drawing value due to tension in the plate thickness direction at the center of plate thickness. Therefore, it is desirable to reduce S as much as possible, and S is 0.0050% or less. It is preferably 0.0020% or less.

Al: 0.002 to 0.100%
Al acts as a deoxidizer and is most commonly used in the molten steel deoxidation process. Further, it has the effect of fixing the solid solution N in the steel to form AlN and suppressing the deterioration of toughness due to the reduction of the solid solution N. In order to obtain this effect, Al needs to be contained in an amount of 0.002% or more. It is preferably 0.010% or more. More preferably, it is 0.020% or more. On the other hand, if the content exceeds 0.100%, it diffuses into the weld metal portion during welding and the toughness of the weld metal deteriorates, so the content is set to 0.100% or less. It is preferably 0.070% or less. More preferably, it is 0.060% or less.

Ni: 5.0-10.0%
Ni is an element that is extremely effective in improving the low temperature toughness of steel sheets by increasing the strength of the steel sheets and stabilizing retained austenite. Since Ni is an expensive element, the cost of steel sheet increases as its content increases. Therefore, the Ni content is set to 10.0% or less. On the other hand, when the Ni content is less than 5.0%, the strength of the steel sheet is lowered, and stable retained austenite cannot be obtained at a low temperature, and as a result, the low temperature toughness and strength of the steel sheet are lowered. Therefore, Ni is set to 5.0% or more. Preferably, it is 6.0 to 9.0%.

N: 0.0010 to 0.0080%
N is an austenite stabilizing element and is an element effective for improving cryogenic toughness. Further, it has an effect of suppressing stress corrosion cracking as a trap site of diffusible hydrogen by binding to Nb, V and Ti and finely precipitating as a nitride or carbonitride. In order to obtain such an effect, N needs to be contained in an amount of 0.0010% or more. It is preferably 0.0020% or more. On the other hand, if it is contained in excess of 0.0080%, not only the formation of excess nitride or carbonitride is promoted, the amount of solid solution elements is lowered and the corrosion resistance is lowered, but also the toughness and the plate thickness direction at the center of the plate thickness are reduced. The drawing value due to tension decreases. Therefore, N is set to 0.0.0080% or less. It is preferably 0.0060% or less.

In the present invention, for the purpose of further improving the strength and low temperature toughness, in addition to the above essential elements, Cr: 0.01 to 1.50%, Mo: 0.03 to 1.0, if necessary. %, Nb: 0.001 to 0.030%, V: 0.01 to 0.10%, Ti: 0.003 to 0.050%, B: 0.0003 to 0.0100%, Cu: 0. It can contain one or more selected from 01 to 1.00%.

Cr: 0.01 to 1.50%
Cr is an element effective for increasing the strength. In order to obtain the effect, when Cr is contained, is set to 0.01% or more. On the other hand, Cr may be precipitated in the form of nitrides, carbides, carbonitrides, etc. during rolling, and the formation of such precipitates becomes a starting point of corrosion and fracture, and the low temperature toughness is lowered. Therefore, when it is contained, the amount of Cr is set to 1.50% or less. More preferably, the amount of Cr is 1.00% or less.

Mo: 0.03 to 1.0%
Mo is an element effective in suppressing the temper embrittlement susceptibility of a steel sheet, and is also an element capable of obtaining steel sheet strength without impairing low temperature toughness. In order to obtain such an effect, when Mo is contained, the content is 0.03% or more. More preferably, it is more than 0.05%. On the other hand, if it exceeds 1.0%, the low temperature toughness decreases. Therefore, when Mo is contained, the content is preferably 1.0% or less. More preferably, it is 0.30% or less.

Nb: 0.001 to 0.030%
Nb is an element effective for improving the strength of the steel sheet. In order to obtain such an effect, when Nb is contained, the content is 0.001% or more. It is more preferably 0.005% or more, still more preferably 0.007% or more. On the other hand, if it is contained in excess of 0.030%, coarse carbonitride may be precipitated, which may become a starting point of fracture and deteriorate the tensile property in the plate thickness direction at the center of the plate thickness. In addition, the precipitate may become coarse and the toughness of the base metal may be deteriorated. Therefore, when Nb is contained, it is set to 0.030% or less. It is more preferably 0.025% or less, still more preferably 0.022% or less.

V: 0.01 to 0.10%
V is an element effective for improving the strength of the steel sheet. In order to obtain such an effect, when V is contained, the content is 0.01% or more. It is more preferably 0.02% or more, still more preferably 0.03% or more. On the other hand, if it is contained in an amount of more than 0.10%, coarse carbonitride may be precipitated and become a starting point of fracture. In addition, the precipitate may become coarse and the toughness of the base metal may be deteriorated. Therefore, when V is contained, it is set to 0.10% or less. It is more preferably 0.09% or less, still more preferably 0.08% or less.

Ti: 0.003 to 0.050%
Ti is an element that precipitates as a nitride or carbonitride and is effective in improving the strength of a steel sheet. In order to obtain such an effect, when Ti is contained, the content is 0.003% or more. It is more preferably 0.005% or more, still more preferably 0.007% or more. On the other hand, if it is contained in excess of 0.050%, the precipitate may become coarse and the toughness of the base metal may be deteriorated. In addition, coarse carbonitride may precipitate and serve as a starting point for fracture. Therefore, when Ti is contained, it is set to 0.050% or less. It is more preferably 0.035% or less, still more preferably 0.032% or less.

B: 0.0003 to 0.0100%
B is an element effective for improving the strength of the base material. In order to obtain such an effect, when B is contained, the content is 0.0003% or more. On the other hand, if it is contained in excess of 0.0100%, a coarse B precipitate is formed and the toughness is lowered. Therefore, when B is contained, it is set to 0.0100% or less. More preferably, it is 0.0030% or less.

Cu: 0.01-1.00%
Cu is an effective element that enhances the strength of steel sheets by improving hardenability. In order to obtain such an effect, when Cu is contained, the content is 0.01% or more. On the other hand, if the content exceeds 1.00%, the low temperature toughness of the steel sheet is lowered, and the properties of the steel (slab) surface after casting may be deteriorated. Therefore, when Cu is contained, it is set to 1.00% or less. More preferably, it is 0.30% or less.

Further, in the present invention, Sn: 0.01 to 0.30%, Sb: 0.01 to 0.30%, W: more than 0 to 2.00%, Co: more than 0 to 2. Selected from 00%, Ca: 0.0005 to 0.0050%, Mg: 0.0005 to 0.0050%, Zr: 0.0005 to 0.0050%, REM: 0.0010 to 0.0100%. It can contain one or more.

Sn: 0.01 to 0.30%
Sn is an element effective for improving corrosion resistance. These elements are effective even if they are contained in a small amount, but when Sn is contained, the content is 0.01% or more. However, if it is contained in a large amount, the weldability and toughness are deteriorated, which is disadvantageous from the viewpoint of cost. Therefore, when Sn is contained, it is set to 0.30% or less. More preferably, it is 0.25% or less.

Sb: 0.01 to 0.30%
Similar to Sn, Sb is an element effective for improving corrosion resistance. These elements are effective even if they are contained in a small amount, but when Sb is contained, the content is 0.01% or more. However, if it is contained in a large amount, the weldability and toughness are deteriorated, which is disadvantageous from the viewpoint of cost. Therefore, when Sb is contained, it is set to 0.30% or less. More preferably, it is 0.25% or less.

W: Over 0 to 2.00%
Like Sn and Sb, W is an element effective for improving corrosion resistance. Since these elements are effective even when contained in a small amount, W can be contained in excess of 0%. However, if it is contained in a large amount, the weldability and toughness are deteriorated, which is disadvantageous from the viewpoint of cost. Therefore, when W is contained, it is set to 2.00% or less. More preferably, it is 0.50% or less.

Co: Over 0 to 2.00%
Co is an element effective for improving corrosion resistance, like Sn, Sb, and W. Since these elements are effective even when contained in a small amount, Co can be contained in excess of 0%. More preferably, it is 0.10% or more. However, if it is contained in a large amount, the weldability and toughness are deteriorated, which is disadvantageous from the viewpoint of cost. Therefore, when Co is contained, it is set to 2.00% or less. More preferably, it is 1.50% or less.

Ca: 0.0005 to 0.0050%
Ca is an element effective for controlling the morphology of inclusions such as MnS, and can be contained as needed. Morphological control of inclusions means that the expanded sulfide-based inclusions are made into granular inclusions. Through the morphological control of the inclusions, the tensile properties in the plate thickness direction, the toughness, and the sulfide stress corrosion cracking resistance of the central portion of the plate thickness can be improved. In order to obtain such an effect, when Ca is contained, the content is 0.0005% or more. More preferably, it is 0.0010% or more. On the other hand, when a large amount of Ca is contained, the amount of non-metal inclusions increases, and the tensile characteristics in the plate thickness direction at the center of the plate thickness may decrease. Therefore, when Ca is contained, it is set to 0.0050% or less. More preferably, it is 0.0040% or less.

Mg: 0.0005-0.0050%
Like Ca, Mg is an element effective for controlling the morphology of inclusions such as MnS, and can be contained as needed. Through the morphological control of the inclusions, the tensile properties in the plate thickness direction, the toughness, and the sulfide stress corrosion cracking resistance of the central portion of the plate thickness can be improved. In order to obtain such an effect, when Mg is contained, the content is 0.0005% or more. More preferably, it is 0.0010% or more. On the other hand, when a large amount of Mg is contained, the amount of non-metal inclusions increases, and the tensile characteristics in the plate thickness direction at the center of the plate thickness may decrease. Therefore, when Mg is contained, it is set to 0.0050% or less. More preferably, it is 0.0040% or less.

Zr: 0.0005-0.0050%
Like Ca and Mg, Zr is an element effective for controlling the morphology of inclusions such as MnS, and can be contained as needed. Through the morphological control of the inclusions, the tensile properties in the plate thickness direction, the toughness, and the sulfide stress corrosion cracking resistance at the center of the plate thickness can be improved. In order to obtain such an effect, Zr is set to 0.0005% or more. It is preferably 0.0010% or more. On the other hand, when a large amount of Zr is contained, the amount of non-metal inclusions increases, and the tensile characteristics in the plate thickness direction at the center of the plate thickness may decrease. Therefore, when Zr is contained, it is set to 0.0050% or less. More preferably, it is 0.0040% or less.

REM: 0.0010-0.0100%
Like Ca, Mg, and Zr, REM is an element effective for controlling the morphology of inclusions such as MnS, and can be contained as needed. Through the morphological control of the inclusions, the tensile properties in the plate thickness direction, the toughness, and the sulfide stress corrosion cracking resistance at the center of the plate thickness can be improved. In order to obtain such an effect, the REM is set to 0.0010% or more. More preferably, it is 0.0020% or more. On the other hand, if a large amount of REM is contained, the amount of non-metal inclusions may increase, and the tensile characteristics in the plate thickness direction at the center of the plate thickness may decrease. Therefore, when REM is contained, it should be 0.0100% or less.

The balance is Fe and unavoidable impurities.

Next, the thick steel plate in the present invention has a deformation characteristic in which the drawing value due to tension in the plate thickness direction at the center of the plate thickness is 30% or more. Here, the drawing value is a fraction (ΔS / S (%)) of the amount of decrease in the cross-sectional area of the test piece after the test, ΔS, with respect to the cross-sectional area S of the test piece before the test in the tensile test. By setting the aperture value to 30% or more, the deformation characteristics of the central portion of the plate thickness can be ensured. In the present invention, the aperture value is preferably 35% or more. The drawing value of the present invention can be obtained by controlling the light rolling conditions at the time of casting and / or the conditions at the time of finish rolling, which will be described later.

Further, in the present invention, it is preferable that MnS having a major axis of 100 μm or more is 10 pieces / mm ² or less and the old austenite grains have a circular equivalent diameter of less than 100 μm in the central portion of the plate thickness. This is because stress concentration occurs in casting defects, coarse MnS, and coarse old austenite grains, and is likely to be a starting point of fracture. The desired MnS can be obtained by controlling the light reduction during continuous casting, which will be described later.

Further, the central portion of the plate thickness in the present invention indicates a plate thickness 1/2 position, and the aperture value, MnS and the former austenite grains are the values measured by the measuring method described in Examples described later.

Next, the manufacturing conditions of the present invention will be described. In the following description, the temperature "° C." means the temperature at the center of the plate thickness.

In the method for producing a thick steel sheet of the present invention, a slab having a desired composition is heated to 1000 ° C. or higher and 1300 ° C. or lower, and then during finish rolling, a reduction ratio of 3 or more and at least 2 of the final 3 passes are performed. Hot rolling is performed so that the rolling shape ratio per pass is 0.7 or more.

Reheating temperature of steel material: 1000 ° C or higher and 1300 ° C or lower The reason for reheating the steel material is to dissolve the precipitates in the structure and make the crystal grain size uniform, and the heating temperature is 1000. The temperature is equal to or higher than 1300 ° C. When the heating temperature is less than 1000 ° C., not only the precipitates such as AlN do not dissolve sufficiently, but also they become coarse during reheating and become the starting point of fracture, so that the drawing value in the desired tensile test in the plate thickness direction can be obtained. Absent. On the other hand, when the heating temperature exceeds 1300 ° C., not only the crystal grain size becomes coarse and the toughness deteriorates, but also the production cost increases. Therefore, the reheating temperature is set to 1300 ° C. or lower. The temperature is preferably 1250 ° C or lower, more preferably 1200 ° C or lower. The reheating time is preferably 1 to 10 hours.

The reduction ratio of the finish rolling is 3 or more. During the finish rolling in the hot rolling process, the reduction ratio (slab thickness / final plate thickness) is set to 3 or more to promote recrystallization and sizing, and to achieve porosity. Casting defects such as so-called internal micropores can be crimped to make them harmless. Further, by reducing the central segregation of Mn, P, S and the like, it is possible to obtain a desired tensile property in the plate thickness direction as a desired hot-rolled plate microstructure. In hot rolling with a reduction ratio of less than 3, a desired microstructure cannot be obtained due to residual coarse structure, insufficient detoxification of the casting defects and central segregation, etc., and in a tensile test in a desired plate thickness direction. I can't get the aperture value. Therefore, the reduction ratio is limited to 3 or more. The reduction ratio is preferably 4 or more, and more preferably 5 or more.

Rolling shape ratio per pass for at least 2 of the final 3 passes of finish rolling 0.7 or more Rolled shape ratio per pass for at least 2 of the final 3 passes that finally determine the material By setting the value to 0.7 or more, casting defects can be reliably detoxified, and coarse grains can be suppressed from remaining in the entire steel sheet, particularly in the central portion of the sheet thickness, for sizing. As a result, the drawing value due to tension in the plate thickness direction at the center of the plate thickness is improved. Here, the rolling shape ratio (ld / h _m ) is {the length of the rolled roll in contact with the steel plate (roll contact arc length: ld)} / {the average of the plate thickness on the roll entry side and the plate thickness on the exit side. thickness: refers to _{h m},} represented by formula (1).
_{_{ld / h m = {R (}} h i -h o)} 1/2 / {(h i + 2h o) / 3}
here,
R: Roll radius at each rolling pass h _i : Incoming plate thickness at each rolling pass h ₀ : Outer plate thickness at each rolling pass.
If the number of passes having a rolled shape ratio of 0.7 or more is less than 2 passes, a desired microstructure cannot be obtained, such as a coarse structure remaining or insufficient detoxification of casting defects, and a desired plate thickness center portion. The drawing value due to tension in the plate thickness direction cannot be obtained. Therefore, at least two passes have a rolled shape ratio of 0.7 or more. In order to increase the rolling shape ratio, the rolling roll diameter may be increased or the rolling reduction amount may be increased.

The manufacturing conditions other than the above are not particularly limited, but it is preferable to carry out under the following conditions.

Light reduction during casting In the present invention, it is preferable to lightly reduce the slab during continuous casting. In the present invention, by lightly reducing the pressure, it is possible to further suppress the residual of coarse MnS having a major axis of 100 μm or more and coarse old austenite grains having a circular equivalent diameter of 100 μm or more in the central portion of the plate thickness. As the conditions under light reduction, specifically, it is preferable that the reduction gradient is 0.1 mm / m or more upstream of the final solidification position of the slab.

Cooling start temperature after hot rolling In the present invention, the cooling start temperature after hot rolling is not particularly limited, and is preferably 1000 ° C. or lower and 500 ° C. or higher.

Cooling method after hot rolling In the present invention, the cooling method after hot hot rolling is not particularly limited, and any method such as air cooling or water cooling can be used. In order to obtain necessary properties such as strength and low temperature toughness, water cooling such as spray cooling, mist cooling, and laminar cooling may be performed after hot rolling.

Heat treatment after hot rolling In the present invention, the final product can be cooled after hot rolling, but it is preferable to perform heat treatment in order to further obtain necessary properties such as low temperature toughness. As the heat treatment, it is preferable to perform a tempering treatment after hot rolling. Further, a quenching-tempering treatment may be performed in which a quenching treatment is also performed before the tempering treatment. Further, a two-phase region quenching-tempering treatment in which a tempering treatment is performed after the two-phase region quenching treatment may be performed. Further, the quenching-two-phase quenching-tempering treatment may be performed with the two-phase region quenching treatment sandwiched between the quenching-tempering treatments. It is desirable to manufacture using any of the above processes.

The quenching temperature is preferably Ac ₃ transformation point or more and 1000 ° C. or less. The quenching temperature in the two-phase region is preferably at least the Ac ₁ transformation point and below the Ac ₃ transformation point. The tempering temperature is preferably 500 to 650 ° C.

The Ac ₃ transformation point and the Ac ₁ transformation point can be obtained by the following equations (1) and (2).
Ac ₁ (° C.) = 750.8-26.6C + 17.6Si-11.6Mn-22.9Cu-23Ni + 24.1Cr + 22.5Mo-39.7V-5.7Ti + 232.4Nb-169.4Al ... (1)
Ac ₃ (° C.) = 937.2-436.5C + 56Si-19.7Mn-16.3Cu-26.6Ni-4.9Cr + 38.1Mo + 124.8V + 136.3Ti-19.1Nb + 198.4Al ... (2)
However, the element symbol in the above formulas (1) and (2) represents the content (mass%) of each element, and is set to 0 when the element is not contained.

The steel having the composition shown in Table 1 was melted to form a slab, and then a thick steel plate having a plate thickness of 12 to 70 mm was produced according to the production conditions shown in Table 2. For light reduction, sample No. Under the condition that the reduction gradient was 0.20 mm / m in 1 to 30, the sample No. 31 and 32 were 0.07 mm / m and 0.10 mm / m, respectively.

The obtained thick steel sheet was subjected to the following test.

(Mechanical characteristics in the plate thickness direction)
As for the tensile properties, the thickness direction of the thick steel plate was set to be the tensile direction, and the test piece was processed into a Type A-shaped test piece, and a tensile test was carried out in accordance with JIS G3199. For low temperature toughness, the test piece was collected so that the thickness direction of the thick steel plate was the tensile direction, and the test piece was cooled to -196 ° C in liquid nitrogen and subjected to a Charpy impact test in accordance with JIS Z2242. to determine the absorption energy _{vE -196} at 196 ℃.
In the present invention, the yield strength (YS) is 585 MPa or more, the tensile strength (TS) is 690 MPa or more, and the drawing value after fracture (the amount of decrease in the cross-sectional area of the test piece after the test with respect to the cross-sectional area S of the test piece before the test in the tensile test ΔS). fraction) of 30% or _{more, vE -196} was evaluated as acceptable or 34 J.

(Micro tissue)
From the obtained steel sheet, test pieces for microstructure observation were collected so that the plate thickness 1/2 position was the observation position. The test piece was embedded in resin so that the cross section perpendicular to the rolling direction was the observation surface, and mirror-polished. Next, after carrying out picric acid corrosion, observation was performed with an SEM at a magnification of 200 times, and an SEM image of the structure at a plate thickness of 1/2 was taken. The images of the five visual fields taken were analyzed by an image analysis device, and the number density of MnS having a major axis of 100 μm or more and the maximum value of the equivalent circle diameter of the old austenite grains were obtained.

Table 2 shows the results obtained from the above.

Examples of the present invention (Samples Nos. 1 to 15, 27 to 29, 31 to 32) satisfy a drawing value of 30% or more, and are excellent in both strength and low temperature toughness. On the other hand, the comparative examples (Sample Nos. 16 to 26, 30) outside the scope of the present invention are inferior in at least one of the drawing value, strength, and low temperature toughness.

Claims

By mass%, C: 0.01-0.15%,
Si: 0.01-1.00%,
Mn: 0.10 to 2.00%,
P: 0.010% or less,
S: 0.0050% or less,
Al: 0.002 to 0.100%,
Ni: 5.0-10.0%,
N: A thick steel sheet containing 0.0010 to 0.0080%, having a component composition consisting of the balance Fe and unavoidable impurities, and having a drawing value of 30% or more due to tension in the plate thickness direction at the center of the plate thickness.
Further, in mass%, Cr: 0.01 to 1.50%,
Mo: 0.03 to 1.0%,
Nb: 0.001 to 0.030%,
V: 0.01 to 0.10%,
Ti: 0.003 to 0.050%,
B: 0.0003 to 0.0100%,
Cu: The thick steel sheet according to claim 1, which contains one or more selected from 0.01 to 1.00%.
Further, in mass%, Sn: 0.01 to 0.30%,
Sb: 0.01-0.30%,
W: Over 0 to 2.00%,
Co: Over 0 to 2.00%,
Ca: 0.0005 to 0.0050%,
Mg: 0.0005-0.0050%,
Zr: 0.0005-0.0050%,
REM: The thick steel sheet according to claim 1 or 2, which contains one or more selected from 0.0010 to 0.0100%.
After heating the slab having the component composition according to any one of claims 1 to 3 to 1000 ° C. or higher and 1300 ° C. or lower, at the time of finish rolling, the rolling reduction ratio is 3 or more and at least 2 out of the final 3 passes are 1 A method for manufacturing a thick steel sheet that is hot-rolled so that the rolling shape ratio per pass is 0.7 or more.